CN108531776A - A kind of high-strength titanium matrix composite of brake system of car powder metallurgy and preparation method thereof - Google Patents
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
The present invention relates to a kind of high-strength titanium matrix composites of brake system of car powder metallurgy and preparation method thereof.The composite material is by titanium alloy substrate and the reinforcing phase composition being uniformly distributed in matrix；The hardening constituent is high-entropy alloy particle；Described matrix is with atomic percentage, including following components：Fe10 15%；Mn3 5%；Nb2 4%；Sn2 4%；Residual components are titanium.The high-entropy alloy presses atomic ratio 1 by Fe, Co, Cr, Ni, Mo:1:1:1:0.15 composition.Preparation method is：Matrix powder and high entropy prealloy powder compression moulding and are sintered after mixing, obtain the titanium matrix composite of high-entropy alloy particle enhancing.Present invention process process is simple, obtains the high-strength titanium matrix composite of powder using conventional powder metallurgical production technology, fastener can also be prepared by way of hot forging, and the high-strength titanium matrix composite fastener of the powder for obtaining high-compactness simultaneously.
Description
Technical field
The present invention relates to powder metallurgy titanium alloy technical field of composite materials, more particularly to a kind of brake system of car powder
Last metallurgical high-strength titanium matrix composite and preparation method thereof.
Background technology
Titanium alloy has many advantages, such as good corrosion resistance, high specific strength, antifatigue, nonmagnetic, suitable for making fastener material
It uses.Titanium alloy is widely applied in aerospace field, to improving the propulsive force of aircraft and spacecraft, increasing voyage,
Fuel is saved, it is significant to reduce launching costs etc..But the high cost of titanium limits the extensive use of titanium alloy, especially
In motor vehicles for civilian use field.And titanium alloy fastener manufacturing cost is high, and wear-resisting property is bad, is especially ground to adhesive wear and fine motion
Damage it is very sensitive, limit its application range.
The production method of titanium alloy fastener can be divided into three kinds at present：1) cast, 2) forging, 3) powder metallurgy.Casting
Method can prepare complex-shaped titanium alloy parts, at low cost, but it is inclined that forming component is easy in casting cooling procedure
The defects of analysis, shrinkage porosite, shrinkage cavity.The titanium alloy parts function admirable prepared is forged, but preparation flow is complicated, melting and forging
Energy consumption is big, and equipment investment is more, and spillage of material is big, and machining amount is big.PM technique has near-net-shape, technique stream
The series of advantages such as journey is short, and the uniform ingredient of titanium alloy product fine microstructures is controllable, have the work for significantly decreasing material cost
With, be manufacture low-cost titanium alloy fastener one of ideal technology.
But simple titanium alloy has been difficult to meet existing demand.Then people begin attempt to design and prepare new titanium
Based composites；Such as in order to improve the abrasion resistance properties of titanium alloy, generally use surface is modified and the technologies such as coating change titanium
Alloy surface ingredient or tissue assign the performances such as high surface hardness, wear-resistant and anticorrosion with this.But face coat is closed with titanium
Auri body chemical composition is different, and coefficient of thermal expansion difference is larger, and bond strength is not high, under fine motion friction and long-term stress effect
Easy to produce peeling；Gas carburizing easily causes titanium alloy " hydrogen embrittlement " mainly with hydrogen-containing gas such as methane, acetylene for " carbon source "；
In Case hardening techniques, the modified layer that ion implanting, nitridation are formed is thin, and durability is poor；What electron beam and laser beam were formed changes
Property layer is easily the defects of surface cracks.During the current particulate metal matrix composites prepared using powder metallurgic method easily
The phenomenon that reacting between reinforced phase and matrix and generating brittlement phase, above-mentioned phenomenon once occur, the performance of products obtained therefrom
It will sharp-decay.Therefore, it is necessary to explore a kind of titanium alloy preparation method of new high-strength wearable.
Invention content
In order to overcome the above-mentioned deficiencies of the prior art, the present invention provides a kind of brake system of car powder metallurgy is high-strength
Titanium matrix composite and preparation method thereof.
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention, a kind of brake system of car
By titanium alloy substrate and it is uniformly distributed in titanium alloy-based internal reinforcing phase composition with the high-strength titanium matrix composite of powder metallurgy；Institute
It is high-entropy alloy particle to state hardening constituent；The titanium alloy substrate is with atomic percentage, including following components：
Fe 10-15%, preferably 10.5-13.5%, further preferably 10.5-11.8%；
Mn 3-5%, preferably 3-4%, further preferably 3-3.5%；
Nb 2-4%, preferably 2.5-3.5%, further preferably 2.8-3.2%；
Sn 2-4%, preferably 2.5-3.5%, further preferably 2.8-3.2%；
Residual components are titanium and inevitable impurity.
Certainly, titanium alloy substrate with the content of atomic percentage Mn be 3%~3.05%, 3.06~3.1%, 3.11%
~3.15%, 3.16%~3.2%, 3.21~3.26%, 3.27%~3.32%, 3.33%~3.35%, 3.36~
3.4%, 3.41%~3.45%, 3.46%~3.5% it is equally applicable to preferred embodiment of the invention.
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention, high-entropy alloy by Fe, Co, Cr,
Ni, Mo press atomic ratio, Fe：Co：Cr：Ni：Mo=1:1:1:1:0.15 composition.As a further preference, the high-entropy alloy
Include stating component with atomic percentage：
Fe 24.1%；
Co 24.1%；
Cr 24.1%；
Ni 24.1%；
Mo 3.6%.
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention, in high-entropy alloy inevitably
Impurity is less than 0.05%.
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention, high-entropy alloy reinforced particulate account for
The 2%-10% of the high-strength titanium matrix composite total weight of brake system of car powder metallurgy, it is preferably 2-6%, further preferred
For 3-5%.
A kind of high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention, the brake system of car powder
In last metallurgical high-strength titanium matrix composite, the granularity of high-entropy alloy particle is 30-100 microns.
A kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention；Including following steps
Suddenly：
Step 1
FeCoCrNiMo high-entropy alloy powder to particle size range at 30-100 microns is fitted into ball mill, carries out wet ball grinding
It handles, after ball milling, is dried under protective atmosphere；Obtain spare high-entropy alloy powder；When the wet ball grinding processing,
Control ball material mass ratio is 5-15：1, it is preferably 10:1；Control rotational speed of ball-mill is 200-450r/min, preferably 300r/min；
Ball-milling Time is controlled to be more than or equal to 15 hours, preferably 18-24 hours；By setting ratio, with the element powder for taking titanium alloy substrate
Last and spare high-entropy alloy powder；After mixing, mixed-powder is obtained；The raw material powder of the titanium alloy substrate includes titanium source
Powder, source of iron powder, manganese source powder, niobium source power, tin source powder；The FeCoCrNiMo high-entropy alloys powder is aerosolization powder；
Or
By setting ratio, the FeCoCrNiMo with the element powders and particle size range for taking titanium alloy substrate at 30-100 microns
Aerosolization high-entropy alloy powder；Carry out high-energy ball milling at least 15 hours, preferably 18-24 hours, further preferably 20 hours；
Obtain mixed-powder；The raw material powder of the titanium alloy substrate include titanium source powder, source of iron powder, manganese source powder, niobium source power,
Tin source powder；Control ball material mass ratio is 5-15 when the high-energy ball milling:1, it is preferably 10:1, control rotational speed of ball-mill is 200-
450r/min, preferably 300r/min；
Step 2
Compression moulding is carried out to mixed-powder, obtains green compact；Then green compact are sintered, obtain sintered blank；
Or
Discharge plasma sintering is carried out to mixed-powder；Obtain sintered blank.
Inventor has found during the experiment, if high-entropy alloy powder is without ball milling；Directly with taking titanium alloy substrate
Element powders mixing (even if other conditions using the present invention designed by corresponding parameter)；The performance of products obtained therefrom is bad.
It is industrial in application, in step 1, when wet ball grinding, use alcohol as protective；Alcohol, ball, ball milling shared by material
The 50-70% of cavity volume.After ball milling, powder is put into vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
Titanium source powder described in a kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention
End, source of iron powder, manganese source powder, niobium source power, tin source powder granularity be 10-100 microns；And source of iron powder, manganese source powder
In end, niobium source power, tin source powder, oxygen content is respectively less than 5ppm, and oxygen content is less than 500ppm in titanium source powder.
Titanium source powder described in a kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention
End is selected from least one of titanium valve, hydrogenation dehydrogenation titanium powder, hydride powder, Ti-M alloyed powders；The M is selected from Fe, Mn, Nb, Sn
At least one of；
The source of iron powder is selected from least one of iron powder, iron alloy powder；The iron alloy powder be iron and Ti, Mn, Nb,
The alloyed powder of at least one of Sn compositions；
The manganese source powder is selected from least one of manganese powder, manganese alloy powder；The manganese alloy powder be manganese and Ti, Fe, Nb,
The alloyed powder of at least one of Sn compositions；
The tin source powder is selected from least one of glass putty, tin alloy powder；The tin alloy powder be tin and Ti, Fe, Nb,
The alloyed powder of at least one of Mn compositions.
A kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention；In step 3,
When mixed-powder is pressed, control pressing pressure is 150-300MPa, the dwell time is 2-5 minutes；Obtain green compact；
The green compact carry out vacuum-sintering, obtain sintered blank；When vacuum-sintering, control vacuum degree is less than or equal to 5 × 10-3Pa, control are burnt
Junction temperature is 1100-1300 DEG C, preferably 1200 DEG C；Time is 1-3 hours, preferably 70min-100min.
A kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention；In step 3,
When carrying out discharge plasma sintering to mixed-powder, control sintering temperature is 850-1000 DEG C, preferably 900~950 DEG C, controls
Pressure is 20-100MPa, preferably 50MPa, and the control dwell time is 2-10min, preferably 5min；Obtain sintered blank.
A kind of preparation method of the high-strength titanium matrix composite of brake system of car powder metallurgy of the present invention；Gained sintered blank
After pyroplastic deformation, the high-strength titanium matrix composite fastener of brake system of car powder metallurgy that is sized；Institute
It includes hot forging to state pyroplastic deformation；Before the hot forging, the preheating temperature for controlling mold is 300-500 DEG C, is preferably 350
℃；Controlled at 800-1000 DEG C when stating hot forging.
The high-strength titanium matrix composite of brake system of car powder metallurgy that is of the invention designed and preparing, after optimized,
Intensity is 98%-98.3% up to 1545-1551MPa, Rockwell hardness 50-52HRC, consistency.
Principle and advantage
Compared with prior art, the present invention its distinguishing feature is：
(1) process is simple, and the production cycle is shorter；Compared to traditional forging, casting technique；Present invention process flow shortens
60-70%；This has been greatly reduced production cost.
(2) equipment needed for production is conventional equipment, can effectively reduce production cost and equipment investment；It is directly processed
Cost be about it is existing forging, casting technique 70-80%；
(3) high-strength titanium matrix composite consistency prepared by the present invention has larger carry than conventional powder metallurgy titanium alloy
Height, and fine microstructures, ingredient is uniform, and high-entropy alloy enhances even particle distribution.
(4) high-strength titanium matrix composite tensile strength prepared by the present invention is better than National Military Standard GJB2219-9 (fastenings
Part titanium alloy bar (line) material specification) and standard GB/T-T2965-2007 (titanium or titanium alloy bar) performance indicator, completely
Meet the size and performance requirement of titanium alloy for fastening piece material.
(5) present invention realizes the Synchronous lifting of titanium matrix composite tensile strength and hardness；And its tensile strength
It is apparently higher than ordinary powder metallurgy titanium alloy material.
In short, the present invention solves existing powder by the component for optimizing matrix alloy with proper amount of specific high-entropy alloy
Last metallurgical technology prepares the problem for easily occurring " brittlement phase " in titanium matrix composite.Simultaneously by high-strength titanium that is designed and preparing
When based composites are used for brake system of car fastener, the performance for being much better than similar product is shown, after optimized, the present invention
The performance of product can even maintain an equal level with avigation piece titanium matrix composite, but cost be only avigation piece 50% and it is following.
Description of the drawings
Fig. 1 is a kind of preparation method technological process designed by the present invention.
Fig. 2 is (a) micro-organization chart and (b) element EDAX results of the high-strength titanium matrix composite of 3 powder of embodiment.
Fig. 3 is the stress strain curve figure of the high-strength titanium matrix composite of 3 powder of embodiment.
As can be seen from Figure 1 the basic procedure of technique designed by the present invention.
As can be seen from Figure 2 the product compactness of the high-strength titanium matrix composite of powder prepared by embodiment 3 is good, gold
It is uniform to belong to fine microstructures, high-entropy alloy enhances even particle distribution, and high-entropy alloy particle generates metallurgical binding with titanium alloy substrate,
Boundary strength is high.
As can be seen from Figure 3 the tensile strength of the high-strength titanium matrix composite of powder prepared by embodiment 3 reaches
1500MPa, fracture elongation is 6.7% or so.Its 3 trial curves essentially coincide, this proves that gained chemical conversion properties of product are steady
It is fixed.
Specific implementation mode
In order to make the object, technical scheme and advantages of the embodiment of the invention clearer, below in conjunction with the embodiment of the present invention
In attached drawing, technical solution in the embodiment of the present invention is explicitly described, it is clear that described embodiment is the present invention
A part of the embodiment, instead of all the embodiments.Based on the embodiments of the present invention, those of ordinary skill in the art are not having
The every other embodiment obtained under the premise of creative work is made, shall fall within the protection scope of the present invention.
Unless otherwise defined, all technical terms used hereinafter with those skilled in the art are normally understood contains
Justice is identical.Technical term used herein is intended merely to the purpose of description specific embodiment, is not intended to limitation present aspect
Protection domain.
The specific implementation process of the present invention is as follows：
FeCoCrNiMo high-entropy alloys powder includes stating component with atomic percentage in embodiment：
Fe 24.1%；
Co 24.1%；
Cr 24.1%；
Ni 24.1%；
Mo 3.6%.
FeCoCrNiMo high-entropy alloys powder is aerosolization powder in the embodiment of the present invention.
In embodiment 1-6, brake system of car fastener that gained composite material is sized after hot forging；Institute
Before stating hot forging, the preheating temperature for controlling mold is 350 DEG C；Controlled at 900 DEG C when stating hot forging.
Embodiment 1：
Preparation method as shown in Figure 1, comprises the steps of：
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:11:3:3:3 weigh.
(2) the FeCoCrNiMo high-entropy alloy powder by particle size range at 30-100 microns is packed into planetary ball mill, carries out
Ball-milling treatment, ball material mass ratio are 10:1, rotating speed 300/min, Ball-milling Time 20 hours, protected alcohol in mechanical milling process.Ball milling
After, powder is put into vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
(3) by ball milling in the TiFeMnNbSn powder weighed in step (1) and step (2), the FeCoCrNiMo high after drying
Entropy alloyed powder (granularity is 10-100 microns) is 49 according to mass ratio:1 ratio is packed into V-type batch mixer, uniformly mixing 10 hours,
The forvacuum before mixing of V-type batch mixer, reinjects argon gas and is protected.
(4) powder being uniformly mixed in step (3) is fitted into flexible rubber package set, then carries out isostatic cool pressing,
Pressure control sloughs rubber package set and obtains green compact in 250MPa or so, pressurize 3 minutes.
(5) green compact will be made in step (4) and is put into vacuum sintering furnace progress vacuum-sintering, vacuum degree control is in 5 ╳ 10- 3Pa, 1200 DEG C of sintering temperature, heat temperature raising speed are 8 DEG C/min heat temperature raising speed, 1.5 hours are kept the temperature, with furnace cooling after heat preservation
But.
The tensile strength of the high-strength titanium matrix composite of powder manufactured in the present embodiment is 1255MPa, Rockwell hardness number
49.8HRC：Consistency is 98.1%.
Embodiment 2
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:10.5:3.3:3.2 weighing.
(2) the FeCoCrNiMo high-entropy alloy powder by particle size range at 30-100 microns is packed into planetary ball mill, carries out
Ball-milling treatment, ball material mass ratio are 10:1, rotating speed 300/min, Ball-milling Time 20 hours, protected alcohol in mechanical milling process.Ball milling
After, powder is put into vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
(3) by FeCoCrNiMo high-entropy alloy powder in the TiFeMnNbSn powder weighed in step (1) and step (2) according to matter
Amount is than being 9:1 ratio is packed into V-type batch mixer, uniformly mixing 10 hours, and the forvacuum before mixing of V-type batch mixer reinjects
Argon gas is protected.
(4) powder being uniformly mixed in step (3) is fitted into flexible rubber package set, then carries out isostatic cool pressing,
Pressure control sloughs rubber package set and obtains green compact in 250MPa or so, pressurize 3 minutes.
(5) green compact will be made in step (4) and is put into vacuum sintering furnace progress vacuum-sintering, vacuum degree control is in 5 ╳ 10- 3Pa, 1220 DEG C of sintering temperature, heat temperature raising speed are 8 DEG C/min, keep the temperature 1.5 hours, furnace cooling after heat preservation.
(6) sintered blank surface coating glass protective liquid made from step (5) is heated to 900 DEG C, then carries out die forging, mould
Have preheating temperature at 350 DEG C, can further obtain the high-strength titanium matrix composite fastener of high-density powder.
The tensile strength of the high-strength titanium matrix composite of powder manufactured in the present embodiment is 1276MPa, Rockwell hardness number
58HRC, consistency 98.3%
Embodiment 3
A kind of preparation method of the high-strength titanium matrix composite of powder as shown in Figure 1, comprises the steps of：
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：79.6:11.8:3:2.8:2.8 weighing.
(2) the FeCoCrNiMo high-entropy alloy powder by particle size range at 30-100 microns is packed into planetary ball mill, carries out
Ball-milling treatment, ball material mass ratio are 10:1, rotating speed 300/min, Ball-milling Time 20 hours, protected alcohol in mechanical milling process.Ball milling
After, powder is put into vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
(3) by Ti, Fe, Mn, Nb, Sn powder weighed in step (2) and FeCoCrNiMo high-entropy alloys powder (granularity 10-
200 microns) according to mass ratio be 47:3 ratio is packed into V-type batch mixer, uniformly mixing 10 hours, and V-type batch mixer is before mixing
Forvacuum reinjects argon gas and is protected.
(4) powder being uniformly mixed in step (3) is fitted into graphite grinding tool, uses and puts under 950 DEG C, 50MPa pressure
Electric plasma agglomeration, pressurize 10 minutes slough surface layer graphite paper and obtain sintered blank.
The metallograph of the high-strength titanium matrix composite of powder manufactured in the present embodiment is as shown in Figure 2.From Figure 2 it can be seen that this hair
The product compactness of the high-strength titanium matrix composite of powder of bright preparation is preferable, metal structure fine uniform, high-entropy alloy enhancing
Grain is evenly distributed.
The tensile strength of the high-strength titanium matrix composite of powder manufactured in the present embodiment is 1551MPa, Rockwell hardness number
52HRC, consistency 98.3%.
Embodiment 4
A kind of preparation method of the high-strength titanium matrix composite of powder as shown in Figure 1, comprises the steps of：
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:11:3:3:3 weigh.
(2) the FeCoCrNiMo high-entropy alloy powder by particle size range at 30-100 microns is packed into planetary ball mill, carries out
Ball-milling treatment, ball material mass ratio are 10:1, rotating speed 300/min, Ball-milling Time 20 hours, protected alcohol in mechanical milling process.Ball milling
After, powder is put into vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
(3) by Ti, Fe, Mn, Nb, Sn powder weighed in step (1) and FeCoCrNiMo high-entropy alloys powder (granularity 50-
150 microns) according to mass ratio be 48.5:1.5 ratio is packed into V-type batch mixer, uniformly mixing 10 hours, and V-type batch mixer is mixed
Forvacuum before closing, reinjects argon gas and is protected.
(4) powder being uniformly mixed in step (2) is packed into graphite jig, then carries out discharge plasma sintering, be sintered
900 DEG C of temperature, pressure control slough surface layer graphite paper and obtain sintered blank in 90MPa or so, pressurize 5 minutes.
The tensile strength of the high-strength titanium matrix composite of powder manufactured in the present embodiment is 1430MPa, Rockwell hardness is
51.2HRC, consistency 98.1%.
Embodiment 5
Other conditions are consistent with embodiment 1；The difference is that：
By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：72:15:5:4:4 weigh.Its products obtained therefrom
Tensile strength is 1120MPa, hardness 40.3HRC, consistency 98.2%.
Embodiment 6
Other conditions are consistent with embodiment 1；The difference is that：
By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：83:10:3:2:2 weigh.Its products obtained therefrom
Tensile strength is 1062MPa, hardness 38.3HRC, consistency 98.3%.
Embodiment 7
Other conditions are consistent with embodiment 4, the difference is that：
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:11:3:3:3 weigh；Obtain raw material
Powder；
(2) in mass ratio, matrix material powder：FeCoCrNiMo high-entropy alloys powder=9:1；With taking raw material powder and granularity
Range 30-100 microns FeCoCrNiMo high-entropy alloys powder and be packed into planetary ball mill, carry out ball-milling treatment, ball material matter
Amount is than being 10:1, rotating speed 300/min, Ball-milling Time 20 hours, protected alcohol in mechanical milling process.After ball milling, powder is put
Enter vacuum drying chamber under the conditions of 80 DEG C, vacuum drying is for use.
Its products obtained therefrom tensile strength is 1480MPa, hardness 63HRC, consistency 98.3%.
Comparative example 1 (is not added with high-entropy alloy and non-ball milling)
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:11:3:3:3 weigh.
(2) Ti, Fe, Mn, Nb, Sn powder weighed in step (1) is packed into V-type batch mixer in proportion, uniformly mixing 10 is small
When, the forvacuum before mixing of V-type batch mixer reinjects argon gas and is protected.
(3) powder being uniformly mixed in step (2) is packed into graphite jig, then carries out discharge plasma sintering, be sintered
900 DEG C of temperature, pressure control slough surface layer graphite paper and obtain sintered blank in 90MPa or so, pressurize 5 minutes.
The tensile strength of powder high-strength titanium alloy material prepared by this comparative example is 1090MPa, Rockwell hardness number
40.5HRC, consistency 98%.There is certain decline compared to the tensile strength of embodiment 4 before and hardness.
Comparative example 2 (without high-energy ball milling)
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Sn powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Sn powder is according to atomic ratio：80:11:3:3:3 weigh.
(2) by Ti, Fe, Mn, Nb, Sn powder weighed in step (1) and FeCoCrNiMo high-entropy alloys powder (granularity 50-
150 microns) according to mass ratio be 9:1 ratio is packed into V-type batch mixer, uniformly mixing 10 hours, and V-type batch mixer is pre- before mixing
It vacuumizes, reinjects argon gas and protected.
(3) powder being uniformly mixed in step (2) is packed into graphite jig, then carries out discharge plasma sintering, be sintered
900 DEG C of temperature, pressure control slough surface layer graphite paper and obtain sintered blank in 90MPa or so, pressurize 10 minutes.This product hardness
Higher about 61.5HRC, plasticity is poor, and wherein tensile strength is also much worse than the embodiment of the present invention.
Comparative example 3 (lacks Sn) in matrix
Other conditions are consistent with embodiment 1, the difference is that,
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) it is raw material (being not added with Sn).A small amount of inevitable impurity element may be contained in raw material；By Ti powder, Fe powder,
Mn powder, Nb powder are according to atomic ratio：83:11:3:3 weigh.
The tensile strength of its products obtained therefrom is 1050MPa, hardness 43HRC：Consistency is 98.1%.
Comparative example 4 (substitutes Sn) with the congeners Si of Sn
Other conditions are consistent with embodiment 1, the difference is that, replace Sn with Si equivalent；
(1) with the hydrogenation and dehydrogenization Ti powder (oxygen content is less than 500ppm) that granularity is -325 mesh, granularity is the hydroxyl of -325 mesh
Fe powder (oxygen content is less than 5ppm), granularity are -250 mesh Mn powder (oxygen content is less than 5ppm), and granularity is -400 mesh Nb powder (oxygen contents
Less than 5ppm) and granularity be -400 mesh Si powder (oxygen content be less than 5ppm) be raw material.It may can not be kept away containing a small amount of in raw material
The impurity element exempted from；By Ti powder, Fe powder, Mn powder, Nb powder, Si powder is according to atomic ratio：80:11:3:3:3 weigh.
The tensile strength of its products obtained therefrom is 1005MPa, hardness is only 42.3：Consistency is 97.6%.
The FeCoCrNiMo high-entropy alloy powder that the present invention is substituted with other high-entropy alloy powder has also been attempted in inventor；But it imitates
Fruit is bad.
Inventor also attempts, and matrix lacks the experiment of Mn, but income effect is also bad.
Claims (10)
1. a kind of high-strength titanium matrix composite of brake system of car powder metallurgy, it is characterised in that：The brake system of car
By titanium alloy substrate and it is uniformly distributed in titanium alloy-based internal reinforcing phase composition with the high-strength titanium matrix composite of powder metallurgy；Institute
It is high-entropy alloy particle to state hardening constituent；The titanium alloy substrate is with atomic percentage, including following components：
The high-entropy alloy presses atomic ratio, Fe by Fe, Co, Cr, Ni, Mo：Co：Cr：Ni：Mo=1:1:1:1:0.15 composition；
High-entropy alloy reinforced particulate accounts for the 2%- of the high-strength titanium matrix composite total weight of brake system of car powder metallurgy
10%.
2. a kind of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 1, feature exist
In；The titanium alloy substrate is with atomic percentage, including following components：
Residual components are titanium and inevitable impurity；
High-entropy alloy reinforced particulate accounts for the 2-6% of the high-strength titanium matrix composite total weight of brake system of car powder metallurgy.
3. a kind of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 2, feature exist
In；The titanium alloy substrate is with atomic percentage, including following components：
Residual components are titanium and inevitable impurity；
High-entropy alloy reinforced particulate accounts for the 3-5% of the high-strength titanium matrix composite total weight of brake system of car powder metallurgy.
4. a kind of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 1, feature exist
In：In the high-strength titanium matrix composite of brake system of car powder metallurgy, the granularity of high-entropy alloy particle is that 30-100 is micro-
Rice.
5. a kind of side preparing the high-strength titanium matrix composite of claim 1-4 any one institute's brake system of car powder metallurgy
Method；It is characterized in that；Include the following steps：
Step 1
FeCoCrNiMo high-entropy alloy powder to particle size range at 30-100 microns is fitted into ball mill, is carried out at wet ball grinding
It manages, after ball milling, is dried under protective atmosphere；Obtain spare high-entropy alloy powder；When the wet ball grinding processing, control
Ball material mass ratio processed is 5-15:1；Control rotational speed of ball-mill is 200-450r/min；Ball-milling Time is controlled to be more than or equal to 15 hours；It presses
Setting ratio, with the element powders and spare high-entropy alloy powder for taking titanium alloy substrate；After mixing, mixed-powder is obtained；
The raw material powder of the titanium alloy substrate includes titanium source powder, source of iron powder, manganese source powder, niobium source power, tin source powder；It is described
FeCoCrNiMo high-entropy alloy powder is aerosolization powder；
Or
By setting ratio, the FeCoCrNiMo aerosols with the element powders and particle size range for taking titanium alloy substrate at 30-100 microns
Change high-entropy alloy powder；Carry out high-energy ball milling at least 15 hours；Obtain mixed-powder；The raw material powder packet of the titanium alloy substrate
Include titanium source powder, source of iron powder, manganese source powder, niobium source power, tin source powder；Control ball material mass ratio is when the high-energy ball milling
5-15:1, control rotational speed of ball-mill is 200-450r/min；
Step 2
Compression moulding is carried out to mixed-powder, obtains green compact；Then green compact are sintered, obtain sintered blank；
Or
Discharge plasma sintering is carried out to mixed-powder；Obtain sintered blank.
6. a kind of preparation side of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 5
Method；It is characterized in that：The titanium source powder, source of iron powder, manganese source powder, niobium source power, tin source powder granularity be 10-
100 microns；And in source of iron powder, manganese source powder, niobium source power, tin source powder, oxygen content is respectively less than 5ppm, oxygen in titanium source powder
Content is less than 500ppm.
7. a kind of preparation side of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 6
Method；It is characterized in that：
The titanium source powder is selected from least one of titanium valve, hydrogenation dehydrogenation titanium powder, hydride powder, Ti-M alloyed powders；The M choosings
From at least one of Fe, Mn, Nb, Sn；
The source of iron powder is selected from least one of iron powder, iron alloy powder；The iron alloy powder is in iron and Ti, Mn, Nb, Sn
At least one composition alloyed powder；
The manganese source powder is selected from least one of manganese powder, manganese alloy powder；The manganese alloy powder is in manganese and Ti, Fe, Nb, Sn
At least one composition alloyed powder；
The niobium source power is selected from least one of niobium powder, niobium alloy powder, and the niobium alloy powder is in niobium and Ti, Fe, Mn, Sn
At least one composition alloyed powder；
The tin source powder is selected from least one of glass putty, tin alloy powder；The tin alloy powder is in tin and Ti, Fe, Nb, Mn
At least one composition alloyed powder.
8. a kind of preparation side of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 5
Method；It is characterized in that：In step 2, when mixed-powder is pressed, control pressing pressure is 150-300MPa, pressurize
Time is 2-5 minutes；Obtain green compact；The green compact carry out vacuum-sintering, obtain sintered blank；When vacuum-sintering, vacuum degree is controlled
Less than or equal to 5 × 10-3Pa, control sintering temperature are 1100-1300 DEG C；Time is 1-3 hours.
9. a kind of preparation side of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 5
Method；It is characterized in that：In step 2, when carrying out discharge plasma sintering to mixed-powder, control sintering temperature is 850-1000
DEG C, control pressure 20-100MPa, the control dwell time is 2-10min；Obtain sintered blank.
10. a kind of preparation side of high-strength titanium matrix composite of brake system of car powder metallurgy according to claim 5
Method；It is characterized in that：Gained sintered blank is after pyroplastic deformation, the brake system of car powder metallurgy height that is sized
Strong titanium matrix composite fastener；The pyroplastic deformation includes hot forging；Before the hot forging, the preheating temperature of mold is controlled
It is 300-500 DEG C；Controlled at 800-1000 DEG C when stating hot forging.
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| CN113355545A (en) * | 2021-06-16 | 2021-09-07 | 北京理工大学 | Preparation method of titanium alloy material |
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| CN114653944A (en) * | 2022-04-27 | 2022-06-24 | 镇江力航新材料科技有限公司 | Preparation method of NiCoCr medium-entropy alloy particle reinforced titanium-based composite material |
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| CN115927910B (en) * | 2022-12-08 | 2024-05-28 | 湖南湘投轻材科技股份有限公司 | Titanium-based composite material brake disc and preparation method thereof |
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